CN103993147B - A kind of cold-rolled steel sheet and preparation method thereof - Google Patents
A kind of cold-rolled steel sheet and preparation method thereof Download PDFInfo
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Abstract
The preparation method that the invention discloses a kind of cold-rolled steel sheet, the method includes: slab sequentially passes through hot rolling, batch, cold rolling, annealing, finishing and straightening, wherein, consisting of of described slab: C:0.001-0.006 weight %, Si:0.01-0.06 weight %, Mn:0.2-0.65 weight %, P:0.02-0.07 weight %, S :��0.015 weight %, Al:0.01-0.08 weight %, Ti:0.001-0.025 weight %, Nb:0.02-0.07 weight %, Fe:99.02-99.74 weight %, surplus is inevitable impurity. Invention additionally discloses the cold-rolled steel sheet prepared by said method. The R of gained steel plateeLFor 200-250MPa, RmFor >=320MPa, A80>=36%, r90>=1.8, n90>=0.2, BH2>=35MPa, has excellent market prospect.
Description
Technical field
The present invention relates to a kind of cold-rolled steel sheet and preparation method thereof.
Background technology
Along with the development of automobile industry, the requirement of automobile sheetsteel is improved constantly by market, and in order to meet the forming requirements of market deep-drawing, the demand of special ultra-deep punching cold-rolling steel sheet seems further urgent.
At present, as the method for the special ultra-deep punching cold-rolling steel sheet of preparation, CN101514392A discloses the continuous annealing process of a kind of deep-draw and extra deep drawing sheet steel. This technique includes: steel plate through cleaning, enters continuous annealing furnace, speed 150��350m/min before annealing, adopts nitrogen hydrogen mixeding gas ejection surface of steel plate, steel plate is protected from oxidation, make steel billet temperature heat to 120��180 DEG C simultaneously; Again steel plate is heated so that it is temperature reaches 750��780 DEG C, and is incubated 40��70s; Then steel plate is cooled to 400��460 DEG C, and is incubated 60��300s and carries out Wetted constructures, be then cooled to room temperature. Owing to adopting overaging annealing process, the carbide in steel is made fully to be precipitated out, it is ensured that household electrical appliances steel plate and Automobile Plate punching performance and ultra-deep punching performance. But, the failing to of this technique is advantageously controlled reinforcement process, it is impossible to obtain the cold-rolled steel sheet that intensity is high and forming property has concurrently, relatively costly.
Summary of the invention
It is an object of the invention to overcome existing cold-rolled steel sheet preparation method to be difficult to obtain intensity and cold-rolled steel sheet that forming property has concurrently and relatively costly defect, it is provided that a kind of to be obtained in that intensity is higher and forming property is better and the cold-rolled steel sheet of the preparation method of lower-cost cold-rolled steel sheet and preparation thereof.
To achieve these goals, the preparation method that the present invention provides a kind of cold-rolled steel sheet, the method includes: slab sequentially passes through hot rolling, batch, cold rolling, annealing, finishing and straightening, wherein,
After hot rolling and before batching, first with the rate of cooling of 65-95 DEG C/s, the intermediate slab obtained after hot rolling is cooled to 700-850 DEG C, then is cooled to the temperature batched with the rate of cooling of 10-30 DEG C/s;
The described temperature batched is 650-750 DEG C;
Described cold rolling reduction ratio is 55-74%;
The mode of described annealing is continuous annealing, in the process of described annealing, the intermediate slab obtained after cold rolling sequentially passes through bringing-up section, soaking zone, cooling section, overaging section and cooling twice section, described cold rolling after the intermediate slab that obtains in described bringing-up section, described soaking zone, a described cooling section, outlet temperature respectively 750-850 DEG C in described overaging section and described cooling twice section, 850-900 DEG C, 140-280 DEG C, 260-350 DEG C, less than 100 DEG C, the time of staying is 20-80s respectively, 20-50s, 240-480s, 50-100s, 100-200s,
The percentage by weight of the constituent of described slab is:: C:0.001-0.006 weight %, Si:0.01-0.06 weight %, Mn:0.2-0.65 weight %, P:0.02-0.07 weight %, S :��0.015 weight %, Al:0.01-0.08 weight %, Ti:0.001-0.025 weight %, Nb:0.02-0.07 weight %, Fe:99.02-99.74 weight %, surplus is inevitable impurity.
The present invention also provides for the cold-rolled steel sheet prepared by said method.
The preparation method adopting the present invention can prepare simply to be had finished product mechanical property and reaches yield strength ReLFor 200-250MPa, tensile strength Rm>=320MPa, elongation after fracture A80>=36%, plastic strain ratio r90>=1.8, work hardening index n90>=0.2, baking hardening value BH2The cold-rolled steel sheet of >=35MPa, has excellent market prospect.
Other features and advantages of the present invention will be described in detail in detailed description of the invention part subsequently.
Accompanying drawing explanation
Accompanying drawing is used to provide a further understanding of the present invention, and constitutes the part of description, is used for explaining the present invention, but is not intended that limitation of the present invention together with detailed description below. In the accompanying drawings:
Fig. 1 is the microstructure picture of the cold-rolled steel sheet of the embodiment of the present invention 1 preparation.
Fig. 2 is the microstructure picture of the cold-rolled steel sheet of the embodiment of the present invention 2 preparation.
Fig. 3 is the microstructure picture of the cold-rolled steel sheet of the embodiment of the present invention 3 preparation.
Fig. 4 is the microstructure picture of the cold-rolled steel sheet of comparative example 1 of the present invention preparation.
Fig. 5 is the microstructure picture of the cold-rolled steel sheet of comparative example 2 of the present invention preparation.
Fig. 6 is the microstructure picture of the cold-rolled steel sheet of comparative example 3 of the present invention preparation.
Fig. 7 is the microstructure picture of the cold-rolled steel sheet of comparative example 4 of the present invention preparation.
Detailed description of the invention
Hereinafter the specific embodiment of the present invention is described in detail. It should be appreciated that detailed description of the invention described herein is merely to illustrate and explains the present invention, it is not limited to the present invention.
The preparation method that the present invention provides a kind of cold-rolled steel sheet, the method includes: slab sequentially passes through hot rolling, batch, cold rolling, annealing, finishing and straightening, wherein, after hot rolling and before batching, first with the rate of cooling of 65-95 DEG C/s, the intermediate slab obtained after hot rolling is cooled to 700-850 DEG C, then is cooled to the temperature batched with the rate of cooling of 10-30 DEG C/s;The described temperature batched is 650-750 DEG C, described cold rolling reduction ratio is 55-74%, the mode of described annealing is continuous annealing, in the process of described annealing, the intermediate slab obtained after cold rolling sequentially passes through bringing-up section, soaking zone, cooling section, overaging section and cooling twice section, described cold rolling after the intermediate slab that obtains in described bringing-up section, described soaking zone, a described cooling section, outlet temperature respectively 750-850 DEG C in described overaging section and described cooling twice section, 850-900 DEG C, 140-280 DEG C, 260-350 DEG C, less than 100 DEG C, the time of staying is 20-80s respectively, 20-50s, 240-480s, 50-100s, 100-200s, the percentage by weight of the constituent of described slab is: C:0.001-0.006 weight %, Si:0.01-0.06 weight %, Mn:0.2-0.65 weight %, P:0.02-0.07 weight %, S :��0.015 weight %, Al:0.01-0.08 weight %, Ti:0.001-0.025 weight %, Nb:0.02-0.07 weight %, Fe:99.02-99.74 weight %, surplus is inevitable impurity.
In the present invention, although being obtained with better intensity and the cold-rolled steel sheet of more excellent forming property when the composition of slab is in above-mentioned scope, but in order to obtain the performance of the cold-rolled steel sheet that enhancing obtains, under preferable case, consisting of of described slab: C:0.001-0.006 weight %, Si:0.01-0.06 weight %, Mn:0.2-0.65 weight %, P:0.02-0.07 weight %, S:0.005-0.015 weight %, Al:0.025-0.075 weight %, Ti:0.005-0.025 weight %, Nb:0.025-0.065 weight %, Fe:99.06-99.71 weight %, surplus is inevitable impurity. more preferably, consisting of of described slab: C:0.002-0.005 weight %, Si:0.01-0.04 weight %, Mn:0.29-0.55 weight %, P:0.025-0.055 weight %, S:0.008-0.013 weight %, Al:0.03-0.07 weight %, Ti:0.009-0.013 weight %, Nb:0.034-0.065 weight %, Fe:99.18-99.6 weight %, surplus is inevitable impurity. when the constituent of described slab is in above-mentioned scope, it is possible to through the present invention hot rolling, batch, cold rolling, annealing, after finishing and straightening technique, prepared intensity is higher and the better cold-rolled steel sheet of forming property.
In the present invention, it is considered to the combination property of purity of steel and product, the carbon content in described slab needs to control in above-mentioned scope, if carbon (C) content is more than 0.005 weight %, then the plasticity of steel plate reduces, and forming property worsens; Furthermore, the content of silicon (Si) needs to control in relatively low scope; Manganese (Mn) can increase the intensity of described slab, and can be combined into MnS with sulfur (S), prevents because of the FeS fire check caused simultaneously, but Mn too high levels, the welding performance of steel can be affected, accordingly, it would be desirable to controlled in above-mentioned scope by the content of Mn. Additionally, phosphorus (P) is as intensified element, it is necessary to be added in above-mentioned scope. Consider the economy of steel making working procedure and the effect of Calcium treatment, S is controlled under the scope of��0.015 weight %. Aluminum (Al) adds primarily as deoxidant element, realizing complete deoxidation, its content requirement is at more than 0.01 weight %, but too high aluminum will affect the welding performance of steel and coating adhesion and uneconomical, therefore, Al content is chosen as 0.01-0.08 weight % and is advisable.Niobium (Nb) main fixed interval (FI) C atom, titanium (Ti) is mainly fixed interval (FI) atom N, makes interstitial atom be removed, obtains pure ferrite matrix.
Described slab can adopt the method for the known continuous casting billet of this area to be prepared, for instance can obtain described continuous casting billet after passing through blast furnace ironmaking, molten iron pretreatment, converter smelting, steel ladle deoxidation, alloying furnace rear refining, LF electrical heating, RH application of vacuum and sheet billet continuous casting. Its condition specifically prepared is well known in the art.
According to the present invention, described hot rolling includes roughing and finish rolling. The bundle temperature of opening of described roughing can for 1150-1250 DEG C, it is preferred to 1190-1240 DEG C; The finishing temperature of described roughing can be 1070-1120 DEG C, more preferably 1080-1110 DEG C. Additionally, the thickness of the intermediate slab after described roughing can be 31-35mm, it is preferred to 32-34mm.
Additionally, the bundle temperature of opening of described finish rolling can for 990-1030 DEG C, it is preferred to 1000-1025 DEG C; The finishing temperature of described finish rolling can be 870-950 DEG C, it is preferred to 890-940 DEG C; The thickness of the intermediate slab after described finish rolling is preferably 3-4mm. In order to reach hot rolling roughing required for open bundle temperature, it is possible to first continuous casting billet is heated in heater before roughing, heats and required open bundle temperature when carrying out roughing to continuous casting billet. The thickness of the intermediate slab obtained after described hot rolling is the thickness of the intermediate slab after described finish rolling here, and after namely referring to after described hot rolling that finish rolling completes.
According to the present invention, twice cooling is adopted to cool down after hot rolling, it is preferable that in situation, after hot rolling and before batching, first with the rate of cooling of 70-90 DEG C/s, the intermediate slab obtained after hot rolling is cooled to 750-810 DEG C, then is cooled to the temperature batched with the rate of cooling of 15-25 DEG C/s. More preferably, in situation, after hot rolling and before batching, first with the rate of cooling of 70-85 DEG C/s, the intermediate slab obtained after hot rolling is cooled to 781-805 DEG C, then is cooled to the temperature batched with the rate of cooling of 18-22 DEG C/s.
According to the invention it is preferred in situation, described in be cooled through laminar flow of water carry out or first with laminar flow of water with the cooling of rate of cooling faster again with air with slower rate of cooling cooling.
According to the invention it is preferred in situation, described in the temperature batched be 670-730 DEG C.
According to the invention it is preferred in situation, described cold rolling reduction ratio is 60-70%.
According to the present invention, under preferable case, described cold rolling after the intermediate slab that the obtains outlet temperature respectively 760-820 DEG C, 860-890 DEG C, 150-250 DEG C, 270-320 DEG C, 75-95 DEG C in described bringing-up section, described soaking zone, a described cooling section, described overaging section and described cooling twice section, the time of staying is 30-60s, 30-40s, 300-360s, 60-80s, 120-180s respectively. More preferably, described cold rolling after the intermediate slab that the obtains outlet temperature respectively 783-815 DEG C, 865-888 DEG C, 158-241 DEG C, 274-297 DEG C, 87-92 DEG C in described bringing-up section, described soaking zone, a described cooling section, described overaging section and described cooling twice section, respectively 33-51s, 32-36s, 339-358s, 68-75s, 148-174s.
At this, the outlet temperature of described bringing-up section refer to described cold rolling after the intermediate slab that obtains enter the temperature of described soaking zone through described bringing-up section; The outlet temperature of described soaking zone refer to described cold rolling after the intermediate slab that obtains enter the temperature of a described cooling section through described soaking zone; The outlet temperature of a described cooling section refer to described cold rolling after the intermediate slab that obtains enter the temperature of described overaging section through a described cooling section; The outlet temperature of described overaging section refer to described cold rolling after the intermediate slab that obtains enter the temperature of described cooling twice section through described overaging section; The outlet temperature of described cooling twice section refer to described cold rolling after the intermediate slab that obtains enter temperature when next step processes through cooling twice section.
According to the present invention, described cold rolling after the intermediate slab that obtains through a described cooling section by described overaging section, can heat up in overaging section, after temperature reaches the maximum temperature set (heating-up time is generally 2-5s), lower the temperature (being undertaken by aerator) can be carried out, after cooling, enter back into described cooling twice section.The maximum temperature of described setting such as can be 300-350 DEG C.
According to the present invention, the mode of heating of described bringing-up section can various heating means known in the field, for the present invention, it is preferred to use the heating means of flame combustion (anaerobic heating).
According to the present invention, the mode of heating of described soaking zone can various heating means known in the field, for instance can adopt the heating means of electricity consumption heating radiation pipe.
According to the present invention, the type of cooling of a described cooling section can be various cooling means known in the field, for instance can use the cooling gas of flowing, as cooled down by blower fan jet. Cooling gas used can be commonly used in the art in the gas of jet cooling, for instance, the mixing gas of nitrogen and hydrogen, wherein the percent by volume of hydrogen is 2-8%.
According to the present invention, the type of cooling of described cooling twice section can be various cooling means known in the field, for instance above-mentioned jet cools down.
According to the present invention, the method for the temperature of described control overaging section can be conventional temperature control method, as long as described overaging section makes in the scope that temperature is 260-350 DEG C of slab. The such as method of the temperature of described control overaging section is that overaging section is heated by electricity consumption heating radiation pipe; When needs are lowered the temperature, it is possible to cooled down by aerator.
According to the invention it is preferred in situation, the elongation percentage of described finishing is 0.7-1.3%, more preferably 1-1.25%.
According to the invention it is preferred in situation, the elongation percentage of described straightening is 0.2-0.7%, more preferably 0.3-0.65%.
According to the present invention, by the elongation percentage of the elongation percentage and described straightening that make described finishing in above-mentioned scope, it is possible to have and ensure plate surface quality and the good effect of plate shape.
The present invention also provides for cold-rolled steel sheet prepared by above-mentioned preparation method.
Cold-rolled steel sheet provided by the invention has excellent mechanical property, it is preferable that the R of described cold-rolled steel sheeteLFor 200-250MPa, more preferably 205-245MPa; Preferably, the tensile strength R of described cold-rolled steel sheetm>=320MPa, more preferably 320-360MPa; Preferably, the elongation after fracture A of described cold-rolled steel sheet80>=36%, more preferably 37-42%; Preferably, the plastic strain ratio r of described cold-rolled steel sheet90>=1.8, more preferably 1.8-2.4; Preferably, the work hardening index n of described cold-rolled steel sheet90>=0.2, more preferably 0.2-0.25. Preferably, the baking hardening value BH of described cold-rolled steel sheet2>=35MPa, more preferably 35-65MPa.
The microscopic structure of cold-rolled steel sheet provided by the invention is the ferritic structure of 100%, and ferrite grain size is 7.5-9.5 level, and ferrite grain size is 14-24 ��m.
Cold-rolled steel sheet provided by the invention is owing to intensity is high and forming property is excellent, therefore, when making the steel band becoming specified intensity, cold-rolled steel sheet in the present invention can have thinner thickness, thus decreasing steel consumption, and reduce production cost, there is excellent market prospect.
Hereinafter will be described the present invention by embodiment.
Yield strength R in following example and comparative exampleeL, tensile strength Rm, elongation after fracture A80Method of testing carry out according to GBT228-2002 metal material tensile testing at ambient temperature; Plastic strain ratio r90Method of testing carry out according to the assay method of GBT5027-2007 metal sheet and strip plastic strain ratio (r value); Work hardening index n90Method of testing carry out according to GBT5028-2008 sheet metal and strip elongation strain hardenability value (n value) test method;Baking hardening value (BH2) method of testing carry out according to the part 1 baking hardened steel test method of GBT20564.1-2007 automobile high-strength cold continuous rolling steel plate and steel band.
The continuous annealing unit used in following example and comparative example includes bringing-up section, soaking zone, cooling section, overaging section and cooling twice section successively. Described bringing-up section is that non-oxidation furnace (NOF) is heated by coal gas directly fire, and described soaking zone is heated by electrical heating radial canal; A described cooling section is cooled down by jet; Described overaging section carries out temperature control by electricity consumption heating radiation pipe; Described cooling twice section is cooled down by jet.
Embodiment 1-3
The present embodiment is for cold-rolled steel sheet that the present invention is described and preparation method thereof.
At converter smelting, the continuous casting billet obtaining the present invention through LF stove Ca process, RH decarburization and continuous casting, its constituent is in Table 1. This continuous casting steel billet is heated in heating furnace opening bundle temperature and entering reversible roughing mills to roughing, intermediate blank after roughing enters Coil Box, band steel toe, tail is made to exchange, then finish rolling is carried out, it is quickly cooled to final cooling temperature, then to carry out after layer speed of cooling section cooling to coiling temperature batching (hot rolling technology and cooling technique carry out) according to the condition in table 2 after finish rolling and according to the rate of cooling specified. According still further to the cold rolling and continuous annealing process shown in table 3, slab carried out cold rolling and make annealing treatment, it is about to the slab after batching on cold-rolling mill, is bundled into the cold-reduced sheet of appointed thickness with the cold rolling reduction ratio specified, this cold-rolled steel sheet is annealed by the unit speed then controlling continuous annealing machine again, described continuous annealing sequentially passes through bringing-up section (NOF), soaking zone (RTH), cooling section (GJS), overaging section section (OAS) and cooling twice section (FCS), carries out finishing and straightening after being subsequently cooled to room temperature according still further to the technique in table 3. The mechanical property of the cold-rolled steel sheet finally given and the data of microscopic structure are in Table 4, and Fig. 1-3 is shown in respectively by the photo of its microscopic structure.
Comparative example 1
According to the method described in embodiment 1, described the difference is that, at converter smelting, different with the constituent of the continuous casting billet that continuous casting obtains through LF stove Ca process, RH decarburization, be shown in Table 1, the performance test results obtaining steel plate is shown in Table 4, and Fig. 4 is shown in respectively by the photo of its microscopic structure.
Comparative example 2
According to the method described in embodiment 1, institute the difference is that, the rate of cooling taked in hot rolling technology is 50 DEG C/s, and the performance test results obtaining steel plate is shown in Table 4, and Fig. 5 is shown in respectively by the photo of its microscopic structure.
Comparative example 3
According to the method described in embodiment 1, institute the difference is that, the cold rolling reduction ratio taked in cold-rolling process is 50%, and the performance test results obtaining steel plate is shown in Table 4, and Fig. 6 is shown in respectively by the photo of its microscopic structure.
Comparative example 4
According to the method described in embodiment 1, institute the difference is that, slab is annealed processing by the continuous annealing process shown in table 3, and the performance test results obtaining steel plate is shown in Table 4, and Fig. 7 is shown in respectively by the photo of its microscopic structure.
Table 1
Table 2
Table 3
Note: OAS maximum temperature represents the cold-rolled steel sheet maximum temperature in OAS section, and heating is 3s to the time of maximum temperature.
Table 4
By the data in table 1-4 it can be seen that adopt the present invention preparation method, it is possible to obtain ReLFor 200-250MPa, tensile strength Rm>=320MPa, elongation after fracture A80>=36%, plastic strain ratio r90>=1.8, work hardening index n90>=0.2, baking hardening value BH2>=35MPa, and microscopic structure is the ferritic structure of 100%, ferrite grain size is 7.5-9.5 level, and ferrite grain size is 14-24 ��m, and intensity is high and forming property is excellent, the cold-rolled steel sheet of low cost.
The preferred embodiment of the present invention described in detail above; but, the present invention is not limited to the detail in above-mentioned embodiment, in the technology concept of the present invention; technical scheme can being carried out multiple simple variant, these simple variant belong to protection scope of the present invention.
It is further to note that, each concrete technical characteristic described in above-mentioned detailed description of the invention, in reconcilable situation, it is possible to be combined by any suitable mode, in order to avoid unnecessary repetition, various possible compound modes are no longer illustrated by the present invention separately.
Additionally, can also carry out combination in any between the various different embodiment of the present invention, as long as it is without prejudice to the thought of the present invention, it should be considered as content disclosed in this invention equally.
Claims (10)
1. a preparation method for cold-rolled steel sheet, the method includes: slab sequentially passes through hot rolling, batch, cold rolling, annealing, finishing and straightening, it is characterised in that
After hot rolling and before batching, first with the rate of cooling of 65-95 DEG C/s, the intermediate slab obtained after hot rolling is cooled to 700-850 DEG C, then is cooled to the temperature batched with the rate of cooling of 10-30 DEG C/s;
The described temperature batched is 650-750 DEG C;
Described cold rolling reduction ratio is 55-74%;
The mode of described annealing is continuous annealing, in the process of described annealing, the intermediate slab obtained after cold rolling sequentially passes through bringing-up section, soaking zone, cooling section, overaging section and cooling twice section, described cold rolling after the intermediate slab that obtains in described bringing-up section, described soaking zone, a described cooling section, outlet temperature respectively 750-850 DEG C in described overaging section and described cooling twice section, 850-900 DEG C, 140-280 DEG C, 260-350 DEG C, less than 100 DEG C, the time of staying is 20-80s respectively, 20-50s, 240-480s, 50-100s, 100-200s,
Consisting of of described slab: C:0.001-0.006 weight %, Si:0.01-0.06 weight %, Mn:0.2-0.65 weight %, P:0.02-0.07 weight %, S :��0.015 weight %, Al:0.01-0.08 weight %, Ti:0.001-0.025 weight %, Nb:0.02-0.07 weight %, Fe:99.02-99.74 weight %, surplus is inevitable impurity; The total amount of described slab is 100 weight %.
2. method according to claim 1, wherein, described hot rolling includes roughing and finish rolling; The start rolling temperature of described roughing is 1150-1250 DEG C, and the finishing temperature of described roughing is 1070-1120 DEG C; The start rolling temperature of described finish rolling is 990-1030 DEG C, and the finishing temperature of described finish rolling is 870-950 DEG C.
3. method according to claim 1, wherein, after hot rolling and before batching, is first cooled to 750-810 DEG C with the rate of cooling of 70-90 DEG C/s by the intermediate slab obtained after hot rolling, then is cooled to the temperature batched with the rate of cooling of 15-25 DEG C/s; The described temperature batched is 670-730 DEG C.
4. method according to claim 1, wherein, described cold rolling reduction ratio is 60-70%.
5. method according to claim 1, wherein, described cold rolling after the intermediate slab that the obtains outlet temperature respectively 760-820 DEG C, 860-890 DEG C, 150-250 DEG C, 270-320 DEG C, 75-95 DEG C in described bringing-up section, described soaking zone, a described cooling section, described overaging section and described cooling twice section, the time of staying is 30-60s, 30-40s, 300-360s, 60-80s, 120-180s respectively.
6. the preparation method according to any one in claim 1-3, wherein, the elongation percentage of described finishing is 0.7-1.3%; The elongation percentage of described straightening is 0.2-0.7%.
7. method according to claim 1, wherein, the consisting of of described slab: C:0.001-0.006 weight %, Si:0.01-0.06 weight %, Mn:0.20-0.65 weight %, P:0.02-0.07 weight %, S:0.005-0.015 weight %, Al:0.025-0.075 weight %, Ti:0.005-0.025 weight %, Nb:0.025-0.065 weight %, Fe:99.06-99.71 weight %, surplus is inevitable impurity; The total amount of described slab is 100 weight %.
8. the cold-rolled steel sheet that prepared by the preparation method according to any one in claim 1-7.
9. cold-rolled steel sheet according to claim 8, wherein, the yield strength R of described cold-rolled steel sheeteLFor 200-250MPa, tensile strength Rm>=320MPa, elongation after fracture A80>=36%, plastic strain ratio r90>=1.8, work hardening index n90>=0.2, baking hardening value BH2��35MPa��
10. cold-rolled steel sheet according to claim 8 or claim 9, wherein, the microscopic structure of described cold-rolled steel sheet is the ferritic structure of 100%, and ferrite grain size is 7.5-9.5 level, and ferrite grain size is 14-24 ��m.
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| CN104611534A (en) * | 2015-02-06 | 2015-05-13 | 攀钢集团攀枝花钢铁研究院有限公司 | Ultra-low carbon cold-roll steel sheet and preparation method thereof |
| CN104694817B (en) * | 2015-03-26 | 2016-11-09 | 攀钢集团西昌钢钒有限公司 | Ultralow carbon cold-rolled steel plate production method |
| CN106756524B (en) * | 2015-11-24 | 2019-03-26 | 上海梅山钢铁股份有限公司 | A kind of chemical barrel cold rolling tinning substrate and its manufacturing method |
| CN107413848A (en) * | 2017-07-29 | 2017-12-01 | 华北理工大学 | A kind of preparation method of cold-rolled steel sheet |
| WO2020067752A1 (en) * | 2018-09-28 | 2020-04-02 | 주식회사 포스코 | High-strength cold rolled steel sheet having high hole expansion ratio, high-strength hot-dip galvanized steel sheet, and manufacturing methods therefor |
| CN111101067A (en) * | 2020-02-06 | 2020-05-05 | 鞍钢蒂森克虏伯汽车钢有限公司 | Hot-dip galvanized steel plate with stable baking hardening performance and production method thereof |
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| CN103103328A (en) * | 2011-11-10 | 2013-05-15 | 攀钢集团研究院有限公司 | Production method of low carbon steel plate and low carbon steel plate |
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2014
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| JPH1161332A (en) * | 1997-08-22 | 1999-03-05 | Kawasaki Steel Corp | Coating/baking hardened type cold rolled steel sheet superior in press formability and aging resistance characteristic |
| KR20010062900A (en) * | 1999-12-21 | 2001-07-09 | 이구택 | A method for manufacturing p added extra low carbon cold rolled steel sheet with superior deep drawability |
| WO2004001084A1 (en) * | 2002-06-25 | 2003-12-31 | Jfe Steel Corporation | High-strength cold rolled steel sheet and process for producing the same |
| CN101736193A (en) * | 2008-11-10 | 2010-06-16 | 攀钢集团研究院有限公司 | Low carbon steel plate and preparation method thereof |
| CN101736144A (en) * | 2008-11-26 | 2010-06-16 | 攀钢集团研究院有限公司 | Continuous annealing method |
| CN101956133A (en) * | 2010-10-29 | 2011-01-26 | 攀钢集团钢铁钒钛股份有限公司 | Low-yield strength anti-ageing continuous annealing cold-roll steel sheet and production method thereof |
| CN102094149A (en) * | 2011-03-08 | 2011-06-15 | 攀钢集团钢铁钒钛股份有限公司 | Niobium-containing high-strength hot-galvanized steel plate and production method thereof |
| CN103103328A (en) * | 2011-11-10 | 2013-05-15 | 攀钢集团研究院有限公司 | Production method of low carbon steel plate and low carbon steel plate |
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| CN103993147A (en) | 2014-08-20 |
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